CN111479938A - Heat-treatment-curable high-carbon steel sheet and method for producing same - Google Patents
Heat-treatment-curable high-carbon steel sheet and method for producing same Download PDFInfo
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- CN111479938A CN111479938A CN201880079911.4A CN201880079911A CN111479938A CN 111479938 A CN111479938 A CN 111479938A CN 201880079911 A CN201880079911 A CN 201880079911A CN 111479938 A CN111479938 A CN 111479938A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/613—Gases; Liquefied or solidified normally gaseous material
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a steel sheet used for parts and the like requiring wear resistance or durability, and more particularly, to a heat-treatment-curable high-carbon steel sheet having improved strength and toughness by heat treatment, and a method for manufacturing the same.
Description
Technical Field
The present invention relates to a steel sheet used for parts and the like requiring wear resistance or durability, and more particularly, to a heat-treatment-curable high-carbon steel sheet having improved strength and toughness by heat treatment, and a method for manufacturing the same.
Background
High carbon steel is generally widely used for parts requiring high strength and high hardness. For example, it is widely used for automobile parts, saw blades, knitting needles, chains, agricultural implements, and the like. This is because high carbon steel has characteristics of high strength and high hardness.
As a method for improving the strength, hardness and toughness of the high-carbon steel, the following patent documents 1 to 4 are known.
Patent document 1 discloses a technique for producing tempered martensite by performing quenching and tempering heat treatment. The conventional quenching and tempering heat treatment method as described above is characterized in that cooling to normal temperature at the time of quenching is performed to obtain a martensite structure, and then a tempered martensite structure is obtained by the tempering heat treatment. However, in this case, a certain fraction or more of retained austenite remains, and thus there is a limitation in improving strength.
In addition, patent document 2 discloses a technique of obtaining a structure of ferrite and pearlite by hot rolling after adding an alloy element such as Cr to ensure strength and ductility. However, in this case, the strength is only about 600MPa, and therefore, the steel cannot be used for members requiring wear resistance.
Patent document 3 discloses a technique for producing fine pearlite by austempering heat treatment, and the strength is improved by cold rolling the fine pearlite at a reduction ratio of 80% or less. However, this process requires a further cold rolling process of 80% or more, and thus has a problem of greatly increasing the manufacturing cost.
Patent document 4 is a technique for manufacturing a high-carbon steel sheet having high strength and high toughness by controlling a microstructure through a two-stage cooling process during an austempering heat treatment, but has a limitation in that the strength is significantly improved because the strength is at a level of 1200 MPa.
The parts require high strength and hardness, while on the other hand it is necessary to minimize breakage due to impact. Therefore, in order to reduce the breakage, it is necessary to improve the toughness. That is, there is an increasing demand for a material having excellent toughness in addition to a material simply having high strength or high hardness.
(patent document 1) Korean patent laid-open No. 10-1055390
(patent document 2) Korean patent laid-open No. 10-1615040
(patent document 3) Korean patent laid-open No. 10-1445868
(patent document 4) Korean patent laid-open No. 10-1300158
Disclosure of Invention
Technical problem to be solved
An object of one aspect of the present invention is to provide a heat treatment hardening type high carbon steel sheet having high hardness while ensuring excellent toughness by optimizing alloy composition and heat treatment conditions without adding expensive alloy elements, and a method for manufacturing the same.
The technical problems to be solved by the present invention are not limited to the above-mentioned technical problems, and other technical problems not mentioned above can be clearly understood by those skilled in the art from the following descriptions.
Technical scheme
An aspect of the present invention provides a heat treatment curable high carbon steel sheet comprising, in wt%: c: 0.65-1.0%, Si: 0.5% or less (excluding 0), Mn: 0.1-2.0%, P: 0.05% or less, S: 0.03% or less, the balance being Fe and unavoidable impurities, and the microstructure comprising, in area fraction, at least one of martensite in an amount of 85% or more, retained austenite in an amount of 5% or less, carbide in an amount of 10% or less, and ferrite phase, and the steel sheet having K representing the degree of material resistance to brittle fractureICIs 15 MPa.m1/2The above.
Another aspect of the present invention provides a method of manufacturing a heat treatment curable high carbon steel sheet, the method comprising the steps of: preparing a steel sheet comprising, in weight%: c: 0.65-1.0%, Si: 0.5% or less (excluding 0), Mn: 0.1-2.0%, P: 0.05% or less, S: 0.03% or less, the balance comprising Fe and inevitable impurities; heating the prepared steel sheet to a heating temperature of Ae3 or higher; cooling the heated steel sheet to a cooling termination temperature (Tc); and performing a post-heat treatment at a temperature of 100 ℃ or higher after the cooling, wherein the cooling termination temperature (Tc) satisfies the following relational expression 1.
[ relational expression 1]
Tc is less than or equal to 374-
Advantageous effects
According to the present invention, there are provided a heat treatment-curable high carbon steel sheet having both hardness and toughness without adding a large amount of expensive alloying elements, and a method for manufacturing the same.
Drawings
Fig. 1 is a schematic diagram showing an example of the fine structure of the present invention.
Fig. 2 is a schematic view schematically showing a heat treatment profile of the manufacturing method of the present invention.
Best mode for carrying out the invention
As a result of intensive studies on techniques for improving the strength, hardness, and toughness of a steel sheet while solving the above-described problems of the prior art, the inventors of the present invention have found that the hardness and toughness of a steel sheet can be greatly improved without adding expensive alloying elements by optimizing the carbon content and appropriately controlling the heat treatment temperature to increase the fraction of martensite, which is a microstructure of the steel sheet, and to reduce the fraction of retained austenite, thereby completing the present invention.
Hereinafter, a heat-treatment-curable high-carbon steel sheet according to one aspect of the present invention will be described in detail. First, the alloy composition of the steel sheet of the present invention will be described in detail (hereinafter, wt%).
Carbon (C): 0.65-1.0%
Carbon is an essential element for improving the strength of the steel sheet, and it is necessary to appropriately add the carbon in order to secure the martensite structure and the dislocation density to be achieved in the present invention. When the carbon content is less than 0.65%, it is difficult to secure a martensite structure having a microstructure of 90 area% or more as a steel sheet after heat treatment. Further, even if the martensite structure is formed, sufficient strength cannot be obtained because the dislocation density is not sufficiently secured inside. On the other hand, when the content of carbon exceeds 1.0%, the formation temperature of martensite is lowered, and thus a large amount of retained austenite remains. When the steel is cooled to a lower temperature in order to reduce the retained austenite, cracks are generated by the heat treatment shock. Therefore, the content of C in the present invention is preferably 0.65 to 1.0%.
Silicon (Si): below 0.5% (except 0%)
Silicon functions as a deoxidizer and also functions to improve the strength of the steel sheet. When the content of Si exceeds 0.5%, the surface of the steel sheet is oxidized to form scale, which causes a problem of lowering the surface quality of the steel sheet, and therefore the Si content in the present invention is preferably 0.5% or less (except 0).
Manganese (Mn): 0.1-2.0%
Manganese improves the strength and hardenability of steel, and also serves to suppress the occurrence of cracks due to S by forming MnS in combination with sulfur (S) inevitably contained in the manufacturing process of steel. In the present invention, in order to obtain the above-described effects, the content of manganese is preferably 0.1% or more. On the other hand, when the content of manganese exceeds 2.0%, there is a problem of leaving a large amount of retained austenite, and therefore the content of Mn in the present invention is preferably 0.1 to 2.0%.
Phosphorus (P): less than 0.05%
Phosphorus is an impurity inevitably contained in steel and an element that segregates at grain boundaries to reduce the toughness of steel, and therefore, it is preferable to control the content of phosphorus as low as possible. In theory, it is advantageous to limit the content of P to 0%, but P is inevitably contained in the manufacturing process. Therefore, it is important to control the upper limit of P, and in the present invention, the upper limit of P is preferably 0.05%.
Sulfur (S): less than 0.03%
Sulfur is an impurity inevitably contained in steel, reacts with manganese to form MnS to increase the content of precipitates, and is an element that causes embrittlement of steel. Therefore, it is preferable to control the sulfur content as low as possible. In theory, it is advantageous to limit the S content to 0%, but S is inevitably contained in the manufacturing process. Therefore, it is important to control the upper limit of S, and in the present invention, the upper limit of S is preferably 0.03%.
In addition to the above components, the present invention contains Fe and inevitable impurities. Moreover, the addition of active ingredients other than the above-mentioned components is not excluded.
Next, the microstructure and the mechanical and physical properties of the heat-treated and hardened steel sheet of the present invention will be described in detail.
The steel sheet of the present invention satisfies the above-described composition system, and preferably contains martensite in an amount of 85 area% or more as a microstructure of the steel sheet. When the martensite is less than 85 area%, it is difficult to sufficiently secure the required hardness. Further, it is preferable that the retained austenite is contained by 5 area% or less. When the retained austenite exceeds 5 area%, there is a problem that it is difficult to sufficiently secure a desired hardness because the hardness is lower than that of martensite. The martensite is preferably tempered martensite.
The carbide and ferrite phases may provide high toughness while maintaining high strength of the steel sheet, however, when the carbide or ferrite phase is too much during the subsequent heat treatment, they are preferably 10 area% or less, and in addition, the fraction of the carbide and ferrite is preferably 1 area% or more in order to secure toughness.
In addition, the balance may contain cementite, bainite, and the like, in addition to the above-described structure.
Further, according to an embodiment of the present invention, the average thickness of the martensite plates is preferably 0.25 μm or less, which is explained in detail with reference to fig. 1, the martensite phase (α') formed in the present invention is formed in the shape shown in fig. 1, which represents the length of the short axis, and when the size of the martensite plate exceeds 0.25 μm, the strength of the martensite phase is reduced, which may reduce the hardness of the steel sheet, and therefore, it is preferable to control the average thickness of the martensite plate to 0.25 μm or less, and in addition, in fig. 1, the presence of ferrite and carbide is shown in addition to the martensite and the retained austenite.
As illustrated in fig. 1 mentioned above, the martensite is formed in a needle-like type in the present invention. In particular, the martensite phase having a thickness of 0.4 μm or less is preferably 70% or more. In this case, high hardness can be ensured.
The heat-treated and solidified steel sheet of the present invention can secure extremely high strength without adding expensive alloying elements. As an example, the hardness of the heat-treated hardened steel sheet of the present invention may be 600Hv or more.
In the heat-treated hardened steel sheet of the present invention, K representing the degree of material resistance to brittle fracture of the steel sheetICPreferably 15MPa m1/2The above. Said KICThe brittle fracture resistance value is shown.
The heat-treated steel sheet of the present invention is characterized in that the hardness and toughness are improved simultaneously to achieve compatibility, and the product of the brittle fracture resistance value and the hardness (Hv) is preferably 14,000Hv MPa m1/2The above.
Hereinafter, the method for manufacturing a heat-treatment-curable high-carbon steel sheet according to the present invention will be described in detail.
First, a steel sheet satisfying the above composition is prepared. The type of the steel sheet applicable to the present invention is not particularly limited as long as it is a steel sheet that can be used in the technical field to which the present invention pertains, and is not classified into a hot-rolled steel sheet, a cold-rolled steel sheet, and the like.
The prepared steel sheet is heated to a temperature of Ae3 ℃ or higher. When the heating temperature is less than Ae3 ℃, austenite cannot be sufficiently formed, and therefore a martensite structure of 90 area% or more cannot be obtained after cooling. Therefore, the heating temperature is preferably Ae3 ℃. The Ae3 temperature represents the boundary temperature that exists as an austenite single phase.
After heating to above said Ae3 ℃, it is preferably maintained for 0.5-15 minutes. This is to achieve complete austenitization in the prepared steel sheet. When the holding time after heating is less than 0.5 minute, it is difficult to achieve uniform austenite, and when the holding time after heating exceeds 15 minutes, austenite becomes excessively coarse, or the heat treatment cost excessively increases.
Cooling the heated steel sheet to a cooling termination temperature (Tc). The cooling termination temperature (Tc) preferably satisfies the following relational expression 1. When the cooling termination temperature (Tc) does not satisfy the relation 1, martensite of 90 area% or more cannot be obtained, and retained austenite of more than 5 area% remains, so that the strength desired in the present invention cannot be secured.
[ relational expression 1]
Tc is less than or equal to 374-
The relation 1 is derived in consideration of the relation between the formation temperature and the termination temperature of martensite, and in consideration of the contents of carbon and manganese which may be formed into ferrite or carbide in a subsequent process and have an important influence on the formation of martensite.
In the present invention, the cooling is preferably ultra-low temperature cooling in which the heated steel sheet is cooled to a subzero temperature. This is because sufficient martensite is ensured, and when the temperature of the heated steel sheet is not lowered to the subzero temperature, the transformation into martensite is incomplete, and a large amount of austenite remains, so that the desired hardness cannot be ensured.
There are various methods for the ultra-low temperature cooling, but the present invention is not particularly limited thereto. As an example, cooling is performed with liquid nitrogen.
The cooling rate in the step of cooling to the cooling termination temperature (Tc) is preferably 70 ℃/sec or more. When the cooling rate is less than 70 c/sec, a large amount of, for example, ferrite, pearlite, bainite, etc. is generated during cooling, and thus a sufficient amount of martensite cannot be obtained.
After the cooling, the subsequent heat treatment is preferably performed at a temperature of 100 ℃ or higher. This is to relax the high-strength structure formed in the cooling process, particularly in the rapid cooling process, and to impart toughness. The heat treatment temperature is preferably 300 ℃ or less, and when the heat treatment temperature exceeds 300 ℃, strength and hardness are excessively decreased. As mentioned above, a portion of ferrite or carbide may be formed during the subsequent heat treatment.
In addition, the subsequent heat treatment preferably has a holding time of 1 to 300 minutes. When the holding time is too short to within 1 minute, it is difficult to ensure sufficient toughness, and when the holding time exceeds 300 minutes, excessive heat treatment costs are required.
In addition, fig. 2 is a graph schematically showing a relationship between time and temperature of the heat treatment process condition of one example of the present invention. As shown in fig. 2, the manufacturing method proposed in the present invention includes a process of heating, cooling, and then performing a post-heat treatment and cooling the prepared steel sheet.
Detailed Description
The present invention will be described more specifically with reference to examples. However, it should be noted that the following examples are only for illustrating the present invention and are described in more detail, and are not intended to limit the scope of the present invention. This is because the scope of the present invention is determined by the contents recited in the claims and the contents reasonably derived therefrom.
(examples)
Steel sheets having the compositions (wt%, balance Fe and inevitable impurities) of the following table 1 were prepared, and then the steel sheets were heated and cooled under the conditions of the following table 2. Thereafter, the microstructure of the steel sheet was observed, and the mechanical and physical properties were measured and shown in table 3 below.
The microstructure was measured using Electron Back Scattering Diffraction (EBSD), and then the fractions of martensite and retained austenite and the average thickness of martensite pieces were measured by image analysis.
The hardness test was a vickers hardness test of each microstructure under a load of 5g for 10 seconds. K representing the degree of material resistance to brittle fractureICIn addition, the displacement of the crack according to the load was measured by a Compact Tension (C-T) test piece and evaluated.
[ Table 1]
| Steel grade | C | Mn | Si | P | S |
| Comparative Steel 1 | 0.61 | 0.39 | 0.20 | 0.013 | 0.002 |
| Invention steel 1 | 0.86 | 0.41 | 0.19 | 0.012 | 0.003 |
| Comparative Steel 2 | 0.85 | 3.1 | 0.2 | 0.015 | 0.003 |
[ Table 2]
Tc is the cooling termination temperature (374-423C (wt%) -30.4 Mn (wt%)) calculated by the relation 1.
In table 2, the cooling rates of inventive example 5, comparative examples 5 and 6 were cooling by water cooling with water pressure and water amount adjusted, cooling to normal temperature, and cooling to sub-zero temperature by adding to liquid nitrogen. The cooling rate of 500 ℃/sec is an approximate rate calculated based on the temperature of the heated steel sheet after being added to liquid nitrogen and cooled to the subzero temperature within 1 to 2 seconds.
[ Table 3]
As shown in Table 3, the brittle fracture resistance values of invention examples 1 to 7 satisfying the alloy composition and the production conditions proposed by the present invention are all 15MPa · m1/2The martensite sheet has an average thickness of 0.25 [ mu ] m or less and contains martensite in a fraction of 85 area% or more. In particular, inventive examples 1 to 7 had a hardness of 600Hv or more and the product of the brittle fracture resistance value and the hardness value was 14,000 Hv.MPa.m1/2As described above, it was confirmed that the composition had excellent balance between hardness and toughness.
In contrast, the steel of comparative example 1 has a low carbon content, thereby showing that the average thickness of the martensite pieces is large and the hardness is poor. In comparative examples 2 and 3, the post-heat treatment temperature was out of the range of the present invention, and there was a problem that hardness and toughness could not be ensured at the same time. Comparative example 4 is a case where the steel sheet has a low heating temperature and fails to form sufficient martensite, and comparative examples 5 and 6 are cases where the cooling rate is slow and fails to form sufficient martensite and fails to have sufficient hardness. In addition, the manganese contents of comparative examples 7 and 8 were higher than the manganese content proposed by the present invention, and therefore the fraction of retained austenite was high, and sufficient hardness could not be secured.
Claims (9)
1. A heat-treatment-curable high-carbon steel sheet comprising, in wt.%: c: 0.65-1.0%, Si: less than 0.5% and 0 excluded, Mn: 0.1-2.0%, P: 0.05% or less, S: 0.03% or less, and the balance of Fe and inevitable impurities,
the fine structure contains at least one of martensite in an amount of 85% or more, retained austenite in an amount of 5% or less, carbide in an amount of 10% or less, and ferrite phase in terms of area fraction,
k of the steel plate representing the degree of material resistance to brittle fractureICIs 15 MPa.m1/2The above.
2. The heat-treatment-curable high-carbon steel sheet as claimed in claim 1, wherein the product of hardness and toughness of the steel sheet is 14,000 Hv-MPa-m1/2The above.
3. The heat-treated solidified type high carbon steel sheet according to claim 1, wherein the martensite flakes have an average thickness of 0.25 μm or less.
4. The heat-treatment-curable high-carbon steel sheet according to claim 1, wherein the martensite phase sheet having a thickness of 0.4 μm or less is 70% or more.
5. A method of manufacturing a heat treatment curable high carbon steel sheet, comprising the steps of:
preparing a steel sheet comprising, in weight%: c: 0.65-1.0%, Si: less than 0.5% and 0 excluded, Mn: 0.1-2.0%, P: 0.05% or less, S: 0.03% or less, the balance comprising Fe and inevitable impurities;
heating the prepared steel sheet to a heating temperature of Ae3 or higher;
cooling the heated steel sheet to a cooling termination temperature (Tc); and
after said cooling, a subsequent heat treatment is carried out at a temperature above 100 ℃,
wherein the cooling termination temperature (Tc) satisfies the following relational expression 1,
[ relational expression 1]
Tc < 374-423C (wt%) -30.4 Mn (wt%).
6. The method for manufacturing a heat-treatment curable high-carbon steel sheet according to claim 5, wherein the heating is performed while being maintained at the heating temperature for 0.5 to 15 minutes.
7. The method for producing a heat-treatment curable high-carbon steel sheet according to claim 5, wherein the cooling rate in the cooling step is 70 ℃/sec or more.
8. The method for manufacturing a heat-treatment hardened high-carbon steel sheet according to claim 5, wherein the cooling is performed using liquid nitrogen.
9. The method for producing a heat-treatment-hardened high-carbon steel sheet according to claim 5, wherein the subsequent heat treatment is performed with a holding time of 1 to 300 minutes.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020170170738A KR102043511B1 (en) | 2017-12-12 | 2017-12-12 | Quenched high carbon steel sheet and method for manufacturing the same |
| KR10-2017-0170738 | 2017-12-12 | ||
| PCT/KR2018/013982 WO2019117483A1 (en) | 2017-12-12 | 2018-11-15 | Thermally-curable high carbon steel sheet and manufacturing method therefor |
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| CN111479938A true CN111479938A (en) | 2020-07-31 |
| CN111479938B CN111479938B (en) | 2022-03-08 |
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| JP (1) | JP7018138B2 (en) |
| KR (1) | KR102043511B1 (en) |
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2018
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| KR20190070167A (en) | 2019-06-20 |
| JP7018138B2 (en) | 2022-02-09 |
| JP2021505772A (en) | 2021-02-18 |
| WO2019117483A1 (en) | 2019-06-20 |
| KR102043511B1 (en) | 2019-11-12 |
| CN111479938B (en) | 2022-03-08 |
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